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Article On the New Eu5Zn2As5O and Eu5Cd2As5O

Gregory M. Darone 1,2, Sviatoslav A. Baranets 1,* and Svilen Bobev 1,*

1 Department of and Biochemistry, University of Delaware, Newark, DE 19716, USA; [email protected] 2 The Charter School of Wilmington, Wilmington, DE 19807, USA * Correspondence: [email protected] (S.B.); [email protected] (S.A.B.); Tel.: +1-302-831-8720 (S.B. & S.A.B.)

 Received: 20 May 2020; Accepted: 1 June 2020; Published: 3 June 2020 

Abstract: The new quaternary phases Eu5Zn2As5O and Eu5Cd2As5O have been synthesized by flux reactions and their structures have been established through single- X-ray diffraction. Both compounds crystallize in the centrosymmetric space Cmcm (No. 63, Z = 4; Pearson symbol oC52), with unit cell parameters a = 4.3457(11) Å, b = 20.897(5) Å, c = 13.571(3) Å; and a = 4.4597(9) Å, b = 21.112(4) Å, c = 13.848(3) Å, for Eu5Zn2As5O and Eu5Cd2As5O, respectively. The crystal structures include one-dimensional double-strands of corner-shared MAs4 tetrahedra (M = Zn, Cd) and As–As bonds that connect the tetrahedra to form pentagonal channels. Four of the five Eu fill the space between the pentagonal channels and one Eu is contained within the channels. An isolated anion O2– is located in a tetrahedral hole formed by four Eu cations. Applying the rules and the Zintl concept to rationalize the chemical bonding in Eu5M2As5O(M = Zn, Cd) reveals that the valence can be counted as follows: 5 [Eu2+] + 2 [M2+] + 3 × × × [As3–] + 2 [As2–] + O2–, which suggests an -deficient configuration. The presumed h+ × hole is confirmed by electronic band structure calculations, where a fully optimized bonding will be attained if an additional is added to move the Fermi level up to a narrow band gap (Eu5Zn2As5O) or pseudo-gap (Eu5Cd2As5O). In order to achieve such a balance, and hence, narrow-gap semiconducting behavior in Eu5M2As5O(M = Zn, Cd), is theorized to be in a mixed-valent Eu2+/ Eu3+ state.

Keywords: ; Zintl phases; europium; mixed valence; ; ;

1. Introduction Zintl phases are -like intermetallic compounds in which from the less electronegative elements to the more electronegative elements occurs. Often, the electron donors are alkali, alkaline , or rare earth , which become cations, while the electron acceptors are typically late d- metals or p-block , which become anions. The latter form polyanionic subunits which feature polar covalent bonding [1–3]. Zintl phases are typically semiconductors; however, variations in bonding within the polyanionic substructure and changes in elemental composition can result in varying electrical properties. The complex bonding patterns and diverse electronic properties found in Zintl phases make them interesting subjects in areas of colossal magnetoresistance, mixed valency, ferromagnetism and antiferromagnetism, and thermoelectricity [4–6]. Within the realm of the “classic” Zintl phases, pnictides are the compounds that are characterized by the most polar covalent bonding due to the relatively high of the group 15 elements, and as such, they possess semiconducting behavior with widely varied band gaps. There are also pnictides that can be considered as extensions of the Zintl concept, as in the case of the BaFe2As2

Crystals 2020, 10, 475; doi:10.3390/cryst10060475 www.mdpi.com/journal/crystals Crystals 2020, 10, 475 2 of 13 family of compounds, where with a critical temperature of nearly 40 K [7] can be achieved. Other -containing Zintl phases have become the standard for materials with ultra-low thermal conductivity, which when coupled with favorable charge transport enables very high values of the thermoelectric figure of merit ZT [8–10]. These interesting properties are related to the complex bonding arrangements that can be realized based on smaller anionic subunits which connect to form a variety of polyanionic motifs—from 1D chains and ribbons, to 2D layers and even into extended 3D frameworks. Over the past 15 years, our research group has systematically explored numerous and rare earth metal pnictide systems. The synthesized compounds have almost exclusively been examples of “classic” Zintl phases, which despite featuring complex crystal and electronic structures, have nevertheless shown excellent adherence to the Zintl–Klemm rules [11–17]. While are typical examples of ionic and can hardly be classified as Zintl phases, various fall under the latter category, displaying covalent bonding with a much higher degree of polarity than found in typical intermetallic compounds. Oxypnictides have garnered increased interest in recent years due to the discovery of superconductivity at relatively high transition temperatures, TC,[18–20]. Many examples have already been studied, and systematic investigations of element substitution and doping have yielded higher and higher transition temperatures, with materials like Sm0.98Th0.2FeAsO0.775F0.225 reaching TC of 58.6 K [21]. Although oxides are not an area of focus for our research group, it occasionally happens that a new oxygen-bearing compound is serendipitously found as a side product in a reaction intended to produce another phase. This is especially true for experiments involving the very reactive alkali and alkaline earth metals, as well as Eu from the rare-earth metal block. A brief exposure to the atmosphere during the sealing of an ampoule or inadvertent reduction of alumina (crucible material) might be all the opportunity necessary for unintended oxygen to find its way into the reaction materials or products, resulting in an unplanned oxide phase. While they are infrequent discoveries in our lab, these uncommon oxygen-stabilized phases have been documented in several previous studies, such as Ca4Bi2O, Ba2Cd3–δBi3O, Ba5Cd2Sb5Ox (0.5 < x < 0.7), Eu5Cd2Sb5O, and Ba5Cd2Sb4O2 [22–26]. This small group is expanded with the two title compounds presented herein. In this paper, the synthetic routes of the title compounds will be described, along with the single-crystal X-ray diffraction and structure determination. A review of the key structural features, such as polyanionic subunit building blocks and connections, and comparisons of bond distances with other relevant compounds, follows. Trends in unit cell dimensions and bond distances with elemental substitution are explored, as well as a rationalization of the structure as a confirmed with electronic structure calculations.

2. Materials and Methods

2.1. Synthesis The handling of the starting materials was performed inside an -filled glove-box and under vacuum. Eu, Zn, Cd, As, and Pb were purchased from Alfa Aesar or Sigma-Aldrich with stated purity greater than 99.9% and were used as received. Neither oxygen nor another oxygenated material was deliberately used. Single crystals of Eu5Zn2As5O and Eu5Cd2As5O were obtained as minor side products of reactions of Eu, M, and As (M = Zn or Cd) using the Pb-metal flux method. For Eu5Cd2As5O, Eu, Cd, and As were measured in an elemental ratio of 22:4:18, respectively, and combined in an alumina crucible with an excess of Pb (ca. 5 based on molar Eu content) and sealed in an evacuated fused silica jacket. The × ampoule was heated in a programmable furnace from 100 to 1000 ◦C at a rate of 200 ◦C/hour, allowed to homogenize at this temperature for 10 h, then cooled to 900 ◦C at a rate of 2 ◦C/hour, allowed to dwell at this temperature for 72 h, and then cooled to 600 ◦C at a rate of 100 ◦C/hour. At 600 ◦C, the ampoule was removed from the furnace, inverted, and spun in a centrifuge for 30 s to separate the Pb Crystals 2020, 10, 475 3 of 13 from the crystals. After that, the ampoule was brought back into the glove-box and cracked open. The obtained crystals were isolated and studied by X-ray diffraction (vide infra). As can be suggested from the loaded ratio, the target phase we aimed to synthesize was Eu21Cd4As18, isostructural to Eu21Cd4Sb18 [27]. However, the majority phase identified for this reaction was the ternary compound, Eu2CdAs2 [28], in the form of very small crystals, with Eu5Cd2As5O occurring as a few distinctly different bar-shaped crystals. A second reaction conducted with an elemental ratio of Eu, Cd, As, and Pb of 26:4:18:100, respectively, using a maximum reaction temperature of 850 ◦C produced polycrystalline Eu14CdAs11 as the majority phase [29], again with Eu5Cd2As5O being present as just 2-3 isolated bar-like crystals, which were easily identifiable by sight and subsequently confirmed by single-crystal X-ray diffraction methods. For Eu5Zn2As5O, a slightly different synthetic route was taken, despite the nominal composition being similar. Elemental ratios of 3:1:3 for Eu, Zn, and As, respectively, were measured and combined in an alumina crucible with an excess of Pb (ca. 5 based on molar Eu content) and sealed in an × evacuated fused silica jacket. The ampoule was heated in a programmable furnace from 100 to 1000 ◦C at a rate of 100 ◦C/hour, allowed to homogenize at this temperature for 24 h, then cooled to 650 ◦C at a rate of 3 ◦C/hour. At 650 ◦C, the ampoule was removed from the furnace, inverted, and spun in a centrifuge for 30 s to separate the Pb from the crystals. The major phase identified for this reaction was Eu11Zn6As12 [30], which was obtained as large needle-shaped crystals, with Eu5Zn2As5O occurring as a few smaller crystals with habits akin to those of the previously described Eu5Cd2As5O. No systematic efforts were made to synthesize either Eu5Zn2As5O or Eu5Cd2As5O in bulk quantities. Apparently, the reported quaternaries were encountered in our reactions by serendipity. A partial oxidation of the starting materials, most likely the Eu metal, is speculated to be the source of oxygen. Targeted attempts to change the previously described reactant ratios and conditions repeatedly resulted in other known ternary Eu–M–As phases as major reaction products, with yields of Eu5Zn2As5O and Eu5Cd2As5O varying from zero to just a few small crystals (out of elemental mixtures totaling 500–600 mg). Direct reactions in sealed Nb tubes were also unsuccessful. In these attempts, instead of the title phases, the products included Nb-bearing [31]. The above to the idea that the formation of said oxyarsenides requires more than just the presence of oxygen, and is quite a complicated process, which has to be studied in greater detail.

2.2. Single-Crystal X-ray Diffraction

Single-crystal X-ray diffraction was performed on several single crystals of Eu5Zn2As5O and Eu5Cd2As5O. Crystals were quickly removed from the glove-box, placed in paratone-N oil, and cut to suitable dimensions (less than 0.10–0.15 mm) under the microscope. Intensity data were gathered on a Bruker Apex-II CCD-based diffractometer (Bruker AXS, Germany). An inert atmosphere of cold at constant temperature of 200(2) K was maintained throughout data collection. A monochromatized Mo Kα radiation (λ = 0.71073 Å) was used for the data collection. Crystals were first checked for quality by quick batch runs, and for the best quality specimens, quarters to hemispheres of data were collected. The Bruker SAINT software package was used for the reduction and integration of the raw data [32]. Semi-empirical absorption correction based on equivalents (i.e., multi-scan) was applied with the SADABS software [33]. The SHELXT and SHELXL programs were used for structure and refinement [34,35]. Selected details from the structure determination are summarized in Table1. The Cambridge Structural Database (CSD) contains relevant crystallographic data for this paper, which can be obtained free of charge via http://www.ccdc.cam.ac.uk/conts/retrieving.html (or from the CCDC, 12 Union Road, Cambridge CB2 1EZ, UK; Fax: +44-1223-336033; E-mail:[email protected]). The positions of all eight heavy unique atoms in the unit cell were found using direct methods. The oxygen position was also suggested by the direct methods solution in the case of Eu5Zn2As5O (better diffracting crystal and better data), while in the case of Eu5Cd2As5O, the oxygen position was deduced from the difference Fourier map. The atomic coordinates were standardized using STRUCTURE TIDY, and anisotropic displacement parameters were included in the final least square refinements [36]. The Crystals 2020, 10, 475 4 of 13

final difference Fourier map was featureless. The refined atomic coordinates and equivalent isotropic displacement parameters are given in Table2.

Table 1. Selected single-crystal data collection and structure refinement parameters for Eu5Zn2As5O and Eu5Cd2As5O.

Chemical Formula Eu5Zn2As5O Eu5Cd2As5O Formula weight/ g mol–1 1281.14 1375.2 Crystal system Orthorhombic Space group Cmcm Z 4 T / K 200(2) a/ Å 4.3457(11) 4.4597(9) b/ Å 20.897(5) 21.112(4) c/ Å 13.571(3) 13.848(3) V/ Å3 1232.5(5) 1303.8(4) –3 ρcalc./ g cm 6.90 7.01 µ(Mo Kα)/ cm–1 421.4 394.2 Independent reflections 1008 870 Goodness-of-fit 1.069 1.074 1 R1 (I > 2 σ (I)) 0.024 0.045 1 wR2 (I > 2σ(I)) 0.051 0.095 1 R1 (all data) 0.028 0.052 1 wR2 (all data) 0.052 0.098 Largest peak and hole/ e- Å–3 2.0; –2.6 3.2; –2.5 · 1 P P P 2 2 2 P 2 2 1/2 2 2 2 2 2 R1= ||Fo|–|Fc||/ |Fo|; wR2=[ [w(Fo –Fc ) ]/ [w(Fo ) ]] , where w = 1/[σ Fo +(A P) +B P], and P = (Fo +2Fc )/3; (A and B are weight coefficients). The corresponding CIFs have been deposited and· have deposition· numbers CSD 2004823 and CSD 2004824.

a Table 2. Refined atomic coordinates and equivalent isotropic displacement parameters (Ueq ) for Eu5Zn2As5O and Eu5Cd2As5O.

2 Atom Site x y z Ueq/ Å

Eu5Zn2As5O Eu1 8f 0 0.27425(2) 0.61838(3) 0.0127(1) Eu2 4c 0 0.09198(3) 1/4 0.0170(1) Eu3 4c 0 0.89812(3) 1/4 0.0109(1) Eu4 4a 0 0 0 0.0119(1) As1 8f 0 0.14921(4) 0.00880(5) 0.0120(1) As2 8f 0 0.48551(4) 0.15898(6) 0.0116(1) As3 4c 0 0.29310(5) 1/4 0.0112(2) Zn 8f 0 0.36524(4) 0.08859(7) 0.0134(1) O 4c 0 0.6503(3) 1/4 0.012(1) Eu5Cd2As5O Eu1 8f 0 0.26895(4) 0.61847(7) 0.0111(3) Eu2 4c 0 0.09462(5) 1/4 0.0136(3) Eu3 4c 0 0.90246(5) 1/4 0.0104(3) Eu4 4a 0 0 0 0.0110(3) As1 8f 0 0.14947(8) 0.0214(1) 0.0102(4) As2 8f 0 0.49163(7) 0.1603(1) 0.0109(4) As3 4c 0 0.2942(1) 1/4 0.0090(5) Cd 8f 0 0.36791(5) 0.0826(1) 0.0112(3) O 4c 0 0.6526(7) 1/4 0.010b a b Ueq is defined as one third of the trace of the orthogonalized Uij tensor. Uiso for O atom in Eu5Cd2As5O was constrained at 0.010 Å2. Crystals 2020, 10, 475 5 of 13

2.3. Electronic Structure Calculations

Electronic structure calculations for both Eu5Zn2As5O and Eu5Cd2As5O were performed using TB–LMTO–ASA code [37] within the von Barth–Hedin implementation of the local density approximation (LDA) functional theory [38]. The refined experimental unit cell parameters and atomic coordinates were employed for the calculations (Table1; Table2). Within the scalar-relativistic LMTO approach, the Eu 4f states were treated as core-like and contained seven unpaired electrons. In such a model, the Eu atoms were considered as being formally divalent and contributed to the band structure by Eu 6s and 5d states. The basic set included 4s, 4p, and 3d orbitals for Zn; 5s, 5p, and 4d orbitals for Cd; 4s and 4p orbitals for As; and 2p orbitals for O. The Eu 6p, As 4d, and O 2s and 3d orbitals were treated using the Löwdin downfolding technique. An introduction of empty spheres was necessary to satisfy the atomic sphere approximations (ASA). The Fermi level was selected as the energy reference (EF = 0 eV). Chemical bonding analysis was performed through the calculation of the energy contribution of all filled electronic states for selected atom pairs using the crystal orbital Hamilton population (COHP) method, as is implemented in TB-LMTO-ASA code [39].

3. Results and Discussion

3.1. Structure Description

Both title compounds, Eu5Zn2As5O and Eu5Cd2As5O, crystallize in the centrosymmetric orthorhombic space group Cmcm (Z = 4, No. 63, Pearson symbol oC52), with a that contains four unique europium positions, one unique zinc/ position, three unique arsenic positions, and one unique oxygen position in the asymmetric unit (Tables1 and2). They adopt the Ba2Cd2Sb5F structure type, which until now included only five compounds: A5Cd2Sb5F(A = Ba, Sr, Eu), Eu Cd Sb O, and Ba Cd Sb Ox (x 0.5–0.7) [24,25]. Interestingly, Eu Zn As O is the first 5 2 5 5 2 5 ≈ 5 2 5 Zn-bearing compound in this small but growing family of compounds, whereas Eu5Cd2As5O is chronologically regarded as the first of this structure type. 9– The polyanionic substructure of Eu5M2As5O can be viewed as pentagonal channels of [M2As5] units running along the crystallographic a-axis (Figure1a). These chain-like fragments are made of MAs4 tetrahedra joined by sharing corners and connected through As–As bonds, producing a pattern isostructural to the previously described Ba5Cd2Sb5F[24]. The two different types of arsenic atoms are those bonded to Zn or Cd only, and those bonded through the homoatomic As–As bond forming the of the pentagonal structure. Not surprisingly, similar but doubled channels are present in the related Eu11Zn6As12 structure [30], which was found as a major product in the synthesis that also 2– produced Eu5Zn2As5O. Between the pentagonal channels, O anions are nestled among four Eu cations (Eu1 and Eu2 sites) with tetrahedral coordination. Selected interatomic distances are presented in Table3. In Eu 5Cd2As5O, the distances around the tetrahedrally coordinated cadmium are 2.680 Å for Cd–As1, 2.825 Å for Cd–As2, and 2.791 Å for Cd–As3. These values are similar to those found in other compounds featuring CdAs4 tetrahedra, for example: 2.618 to 3.033 Å in β-Ca2CdAs2 [28], 2.745 Å in Eu14CdAs11 [29], and 2.717 to 2.841 Å in Rb2Cd5As4 [40]. The sum of the covalent radii [41] is also comparable (2.62 Å), supporting the covalent nature of these interactions. The length for the As2–As2 bond that joins the two chains of corner sharing CdAs4 tetrahedra is 2.483 Å, which is similar to As–As bonds found in other compounds, such as 2.341 to 2.514 Å in Cs2NaAs7 [42], 2.457 Å in Eu11Zn6As12 [30], 2.485 to 2.548 Å in Eu21Zn4A18 [43], 7– 2.488 Å in Eu2Zn2As3 [44], 2.514 Å in Eu5In2As6 [45], and 2.750 Å in the disordered trimer [As3] in Eu14Zn1+xAs11 [46] which indicates strong covalent bonding between the atoms, as this is close to the As–As distance in elemental arsenic, 2.517 Å. Crystals 2020, 10, x FOR PEER REVIEW 6 of 13 Crystals 2020, 10, 475 6 of 13

Figure 1. (a) Combined polyhedral/ball-and-stick view of the crystal structure of Eu5Zn2As5O, viewed 5 2 5 downFigure the 1. (aa-axis.) Combined The unit polyhedral/ball-and-stick cell is outlined. (b–e) Coordination view of the environment crystal structure of Eu of atoms Eu Zn inAs Eu5O,Zn viewed2As5O structure.down the a (-axis.f) Coordination The unit cell polyhedron is outlined. of(b–e the) Coordination O atom. Thermal environm ellipsoidsent of forEu atoms O and in Eu Eu atoms5Zn2As are5O plottedstructure. at the(f) 95%Coordination probability polyhedron level. of the O atom. Thermal ellipsoids for O and Eu atoms are plotted at the 95% probability level.

Table 3. Selected bond distances in Eu5M2As5O(M = Zn, Cd). Selected interatomic distances are presented in Table 3. In Eu5Cd2As5O, the distances around the tetrahedrally coordinated cadmium are 2.680 ÅM for= ZnCd–As1, 2.825 Å for Cd–As2,M and= Cd 2.791 Å for Cd– Atom Pair As3. These values are similar to those foundDistance in other/ Å compounds featuring DistanceCdAs4 tetrahedra,/ Å for example: 2.618 to 3.033 Å in β-Ca2CdAs2 [28], 2.745 Å in Eu14CdAs11 [29], and 2.717 to 2.841 Å in M—As1 2 2.561(1) 2.680(1) × Rb2Cd5As4 [40].M—As2 The sum of the covalent radii [41] 2.689(1) is also comparable (2.62 Å), supporting 2.825(2) the covalent nature of theseM—As3 interactions. The length for the 2.659(1) As2–As2 bond that joins the two 2.791(2) chains of corner sharing CdAsAs2—As24 tetrahedra is 2.483 Å, which is 2.471(2) similar to As–As bonds found in 2.483(4) other compounds, Eu1—As1 3.132(1) 3.180(2) such as 2.341 to 2.514 Å in Cs2NaAs7 [42], 2.457 Å in Eu11Zn6As12 [30], 2.485 to 2.548 Å in Eu21Zn4A18 Eu1—As1 2 3.080(1) 3.121(1) 2 × 2 3 5 2 6 3 7– [43], 2.488 Eu1—As3Å in Eu Zn2As [44], 2.514 Å in Eu In 3.145(1)As [45], and 2.750 Å in the disordered 3.173(1) trimer [As ] × in Eu14Zn1+xAsEu1—O11 [46] which indicates strong covalent 2.382(5) bonding between the atoms, 2.462(10) as this is close to the As–AsEu2—As1 distance in2 elemental arsenic, 2.517 3.485(1)Å. 3.370(2) × Eu2—As2 4 3.346(1) 3.353(2) × Eu2—O 2 2.492(4) 2.543(7) × Table 3. Selected bond distances in Eu5M2As5O (M = Zn, Cd). Eu3—As2 4 3.096(1) 3.171(1) × Eu3—As3 2 3.088(1)M = Zn M = Cd 3.193(2) × Eu4—As1 2Atom Pair 3.120(1) 3.169(2) × Distance / Å Distance / Å Eu4—As2 4 3.077(1) 3.151(1) × M—As1 × 2 2.561(1) 2.680(1) M—As2 2.689(1) 2.825(2) In Eu5Zn2As5O, similar bondM—As3 distance comparisons2.659(1) can be2.791(2) made with comparable compounds. The tetrahedrally coordinatedAs2—As2 zinc has the following2.471(2) distances 2.483(4) to its closest neighbors: 2.561 Å for Zn–As1, 2.689 Å for Zn–As2,Eu1—As1 and 2.659 Å for3.132(1) Zn–As3. These 3.180(2) bond distances are similar to those found in other compounds featuringEu1—As1 ZnAs × 2 4 tetrahedra, 3.080(1) such 3.121(1) as 2.454 to 2.664 Å in K2Zn5As4 [47], 2.592 Å in Ba2ZnAs2 [48], 2.532Eu1—As3 to 2.696 Å× 2 in Eu21 3.145(1)Zn4As 18 [43], 3.173(1) 2.530 to 2.678 Å in Sr2Zn2As3 [44], and 2.36 to 2.64 Å in Eu14Zn1+xAs11 Eu1—O[46] and are comparable2.382(5) to the2.462(10) sum of the covalent radii, 2.46 Å [41],

Crystals 2020, 10, 475 7 of 13 supporting the covalent nature of their interactions. The distance for the As2–As2 bonds that join the two chains of corner sharing ZnAs4 tetrahedra is 2.471 Å, which is again similar to As–As bonds found in other compounds, such as Cs2NaAs7, Eu11Zn6As12, Eu21Zn4A18, Eu2Zn2As3, and Eu5In2As6, discussed previously. Further comparison with another member in this isostructural family, Eu5Cd2Sb5O[25] allows for the observation of atom substitution and changes in unit cell volume and bond distances. Eu5Cd2Sb5O has a unit cell volume of 1509.9(3) Å3, and Eu1–O and Eu2–O distances of 2.528 and 2.634 Å, respectively. Moving up in group 15 and substituting the larger Sb with the smaller As leads to a reduction in the 3 unit cell volume to 1303.7(4) Å in the case of Eu5Cd2As5O. The smaller radius of As results in the reduced size of the polyanionic pentagonal channels, as evidenced by shrinking of the overall unit cell dimensions. As the unit cell volume diminishes, the Eu and O atoms are pushed closer together. Correspondingly, the Eu1–O and Eu2–O distances in Eu5Cd2As5O are slightly shorter, 2.462 Å and 2.543 Å, respectively. Again, the same trend can be seen in substituting Cd with Zn. The Eu5Zn2As5O unit cell volume is 1232.5(5) Å3, with Eu1–O and Eu2–O distances of 2.381 and 2.492 Å, respectively. For comparison, the average Eu–O distances reported in other europium oxypnictide compounds, such as Eu4As2O, Eu3As3TaO, and Eu3Zn2Sb3O14, are 2.54, 2.49, and 2.46 Å, respectively [49–51]. While these compounds have different structural features than the three isostructural compounds discussed above, these bond distances agree well with the distances found in those three compounds.

3.2. Electron Count, Electronic Structure and Possibility of Mixed-Valent State for Europium

Almost all other known compounds that crystallize with the Ba2Cd2Sb5F structure type form with divalent alkaline earth metals. Europium is also nominally divalent and its crystal chemistry 2+ often mirrors that of . Therefore, assuming Eu , the valence electron count in Eu5M2As5O (M = Zn, Cd) can be partitioned as follows: 5 [Eu2+] + 2 [M2+] + 3 [As3–] + 2 [As2–] + O2– + × × × × h+. Such reveals a charge imbalance, since there is one missing positive charge to counterbalance the 15 electrons needed for covalent bonding within the anionic substructure. This conjecture is corroborated in part by the electronic structure calculations, discussed next. Electronic structure calculations were driven by the urge to support the valence electron count presented above. From this, and from the analysis of the respective interatomic distances (Table3), particularly those involving the Eu1–O and Eu2–O interactions, one might argue that a possible explanation for this perceived electron shortage is rooted in the existence of mixed-valent Eu in both Eu5Zn2As5O and Eu5Cd2As5O phases. However, electronic structures of compounds are very challenging to compute, primarily due to complications such as strong spin-orbit coupling and the presence of highly localized 4f electrons which still may take part in bonding interactions. It is common practice in computational -state chemistry to treat the 4f orbitals as core levels, artificially excluding 4f electrons from bonding interactions. In the case of semiconducting materials, this approach has the advantage of avoiding f-states close to the Fermi level, therefore enabling the possibility to at least estimate the band gap. Obviously, such simplification renders impossible the theoretical confirmation of the charge fluctuation on Eu sites (which requires much more advanced calculations), but nevertheless, gives robust support to the conclusions based on the Zintl concept. The electronic densities of states (DOS) for Eu5Zn2As5O and Eu5Cd2As5O are shown in Figure2a,c, respectively. Similar to Ba5Cd2Sb5F and many other Zintl phases, the states close to the Fermi level are mainly contributed to by pnictide-p and alkaline-earth metal or Eu-d orbitals, specifically here by As-p and Eu-d orbitals, indicating orbital mixing and partial covalency of the Eu–As interactions. Intense peaks at ca. –1.5 eV are contributed by Eu and O orbitals, indicating strong ionic Eu–O interactions. The rest of the features in the DOS and the partial DOS are identical to those in Ba5Cd2Sb5F[24] and will not be discussed here. CrystalsCrystals 20202020,, 1010,, x 475 FOR PEER REVIEW 98 of of 13 13

FigureFigure 2. CalculatedCalculated density density of states (DOS) forfor EuEu55Zn2As55OO( (aa)) and Eu5CdCd22AsAs55OO( (cc) )and and partial partial

densitydensity of of states states (PDOS) diagrams ( b)) for Eu atomsatoms inin EuEu55Zn2AsAs55O.O. ( (aa)) Cumulative Cumulative crystal crystal orbital orbital HamiltonHamilton population population (COHP) (COHP) curves curves ( (d–fd–f)) calculated calculated for for Eu Eu55ZnZn22AsAs5O.5O.

ExtendingBoth DOS plotsthis line confirm of thinking, that Eu5Zn we2As also5O andspec Euulate5Cd 2aboutAs5O dothe not possibility have fully of optimized inclusion bonding. of one hydrogenThe corresponding atom per number formula of unit. valence It is electronswell-known for both that compoundsthe commercially is 43 per supplied formula rare unit earth (10 provided metals couldby the contain presumed small divalent amounts Eu of atoms, metal 4 hy provideddride. If by the Zn structure/Cd atoms, contains 25 provided OH– and by not the O As2–, atomsthe charge- and 4 balanceby the O can atom be (LMTOachieved treats without all p-electrons the need offor oxygen Eu2+/Eu as3+ a because valence electrons)).the formula However, can be partitioned an integrated as DOS suggests that 44 electrons per formula will to an optimal number of valence electrons—the follows: (Eu2+)5(M2+)2(As3–)3(As2–)2(OH–). Unfortunately, O2– and OH– are not easily distinguishable by meansFermi levelof X-ray is located diffraction in the data. valence Our band SCXRD in regions data do of highnot offer DOS any in both indication cases. Indeed,of residual at ca. electron 0.45 eV, there is a tiny band gap with Eg 0.02 eV for Eu Zn As O and a pseudogap for Eu Cd As O. Similar density near the oxygen atoms in≈ both structures,5 and2 the5 anisotropic displacement5 parameter2 5 for the electronic structure features were recently reported for numerous A MPn phases (A = Ca, Sr; Yb; oxygen in Eu5Zn2As5O is very symmetric. While this is solid evidence14 11for O2–, OH– cannot be conclusivelyM = Mg, Cd, ruled Zn; Pn out.= As, We Sb) can [29 ,46ar,gue,52,53 ].however, based on the geometric constraints, that the conjectureThe conclusion for that theis improbable. electronic structures As can be of seen Eu5Zn in2 FigureAs5O and 1f, the Eu5 Cdoxygen2As5 Oatom will is be at destabilized the center ofbecause a tetrahedron of the one-electron and closely surrounded shortage is alsoby four in lineEu cations. with the Eu–O electronic contacts structure are very of close, the archetype ranging

Crystals 2020, 10, 475 9 of 13

Ba5Cd2Sb5F[24], which shows the Fermi level falling in a pseudogap. Note that the latter is valence precise and its electron count can be rationalized as follows: Ba Cd Sb F = 5 [Ba2+] + 2 [Cd2+] + 5 2 5 × × 3 [Sb3–] + 2 [Sb2–] + F–. Partial occupation of the oxygen site may help with the balance of the × × positive and negative charges, as in Ba Cd Sb Ox (x 0.5–0.7) [24]; however, the crystallographic 5 2 5 ≈ analyses do not provide any evidence that this could be the case for Eu5Zn2As5O and Eu5Cd2As5O. Therefore, we can consider three separate scenarios that can introduce an additional electron to achieve electron balance. The first possibility is that the source of the electron is aliovalent substitution on Zn (or Cd) sites by trivalent metals with similar atomic radii and preferred tetrahedral coordination, e.g., Al. This hypothesis is reasonable in the sense that if the alumina crucibles were unintentionally reduced during the reaction, one can trace the origins of both O2– and Al3+ in the structure. Unfortunately, the refinements of the occupation factors of the Zn and Cd sites do not show any tendency for deviation from full, which rules out the possible Zn2+/Al3+ and Cd2+/Al3+ exchange. The second possibility is the reducing of a small amount of silica during the reaction, which, if one assumes it leads to Zn2+/Si4+ and Cd2+/Si4+ exchange, can also alleviate the shortage of valence electrons. , just like aluminum, is much lighter than either Zn or Cd, and therefore its presence can be detected by X-ray crystallography. Based on the 100% occupation factors for Zn and Cd, Si should also be ruled out as a substituent on these cation sites. The third possibility for obtaining an additional electron is doping of trivalent rare-earth metals on the Eu sites, and specifically, the possibility for “self-doping”, i.e., the realization of the mixed valent state for Eu. We consider this scenario as the most likely and we would like to focus on this third case in a more detailed manner. Indeed, both Eu5Zn2As5O and Eu5Cd2As5O can be viewed as electron precise, salt-like compounds, where the electron count conforms to the Zintl–Klemm rules [1–3], assuming that one of the five Eu cations is in the Eu(III) state. In that case, Eu5M2As5O, can be rationalized as: 2+ 3+ 2+ 3– 2– 2– (Eu )4(Eu )(M )2(As )3(As )2(O ). The mixed valency of Eu is required to achieve the charge balance and can be proposed as a solution to the one electron deficiency of the formula of the isostructural Eu5Cd2Sb5O phase [25]. Recent reports on the series of quaternary solid A13REMPn11 (A = Ca, Sr; RE = trivalent rare-earth metal; M = Zn, Cd, Mn; Pn = As, Sb, Bi) confirmed that similar electron doping, via substitution of RE3+ on Ca2+/Sr2+ sites, was an effective way to achieve electron balance in these Zintl phases [46,52,54–56]. Extending this line of thinking, we also speculate about the possibility of inclusion of one atom per formula unit. It is well-known that the commercially supplied rare earth metals could contain small amounts of metal . If the structure contains OH– and not O2–, the charge-balance can be achieved without the need for Eu2+/Eu3+ because the formula can be partitioned as follows: 2+ 2+ 3– 2– – 2– – (Eu )5(M )2(As )3(As )2(OH ). Unfortunately, O and OH are not easily distinguishable by means of X-ray diffraction data. Our SCXRD data do not offer any indication of residual electron density near the oxygen atoms in both structures, and the anisotropic displacement parameter for the oxygen in 2– – Eu5Zn2As5O is very symmetric. While this is solid evidence for O , OH cannot be conclusively ruled out. We can argue, however, based on the geometric constraints, that the conjecture for hydroxide is improbable. As can be seen in Figure1f, the oxygen atom is at the center of a tetrahedron and closely surrounded by four Eu cations. Eu–O contacts are very close, ranging from 2.38 to 2.54 Å. If one were to consider the presence of an O–H group in this tight tetrahedral hole, there undoubtedly would be unphysical Eu–H contacts. Important information about the chemical bonding can be drawn from the crystal orbital Hamilton population (COHP) curves presented in Figure2d,f. Since the Fermi level is located in the valence band, the immediate conclusion that follows is that Eu–As interactions have significant bonding character, whereas the bonding character of the Eu–O contacts is not so apparent. As can be seen in Table3, only two Eu atoms (Eu1 and Eu2) are in close proximity of the O2– anion, with the bond lengths differing significantly. Partial COHP for the average Eu2–As contacts (Figure2e) points to weak bonding character in these interactions, in comparison to the total COHP for this bond and partial COHPs Crystals 2020, 10, 475 10 of 13 for Eu1–As, Eu3–As, and Eu4–As, which is also supported by the values of ICOHPs (0.98, 0.37, 1.53, and 1.36 eV/bond for Eu1–As, Eu2–As, Eu3–As, and Eu4–As at the Fermi level, respectively). This is in good agreement with the results for Ba5Cd2Sb5F[24], where the major portion of the Ba states around the Fermi level in the DOS plots originate from the orbitals of Ba3 and Ba4 atoms. Therefore, we can conclude that Eu3, Eu4, and Eu1 atoms are the primary candidates for aliovalent substitution or for adopting the Eu3+ . The average Eu1–As, Eu3–As, and Eu4–As distances are quite similar, whereas Eu2–As distances are much longer, which also fits well with the larger ionic radius for Eu2+ (1.31 Å) compared to the radius of Eu3+ (1.09 Å) and emphasizes the impossibility of the presence of Eu3+ on the Eu2 site, which is also supported by the partial DOS for Eu atoms (Figure2b). In the end, it is worth mentioning that in terms of COHP analysis, Eu1–O and Eu2–O interactions are almost identical (Figure2f).

4. Conclusions

The new quaternary oxyarsenides Eu5Zn2As5O and Eu5Cd2As5O crystallize in the orthorhombic space group Cmcm and are new members of the Ba5Cd2Sb5F-structure type. These compounds are the first examples of the expanding structural chemistry of this family towards Zn- and As-bearing compounds. Both ionic salt-like Eu–O interactions as well as covalent M–As and As–As bonds are observed in the reported phases. Electronic band structure calculations suggest that if the conclusions made from the valence electron count are valid, Eu5Zn2As5O and Eu5Cd2As5O will be examples of narrow band-gap semiconducting materials with a mixed-valent Eu state. Further development of procedures for the bulk synthesis, and subsequent detailed studies of the physical properties, particularly concerning the valence state of Eu in the reported compounds, is necessary for better understanding of their structure and properties.

Author Contributions: Investigation, data curation, formal analysis G.M.D., S.A.B.; validation, visualization, S.A.B; writing—original draft preparation, G.M.D.; writing—review and editing, S.A.B., S.B.; supervision, project administration, S.B. All authors have read and agreed to the published version of the manuscript. Funding: This research was funded by U.S. Department of Energy, Office of Science, Basic Energy Sciences, Award # DE-SC0008885. Conflicts of Interest: The authors declare no conflict of interest.

References

1. Zintl, E. Intermetallische Verbindungen. Angew. Chem. 1939, 52, 1–6. [CrossRef] 2. Schäfer, H.; Eisenman, B.; Müller, W. Zintl Phases-Transitions between Metallic and . Angew. Chem. Int. Ed. 1973, 12, 694–712. 3. Kauzlarich, S.M. Chemistry, Structure and Bonding of Zintl Phases and Ions; Wiley-VCH: Weinheim, Germany, 1996. 4. Ovchinnikov, A.; Bobev, S. Zintl phases with group 15 elements and the transition metals: A brief overview of pnictides with diverse and complex structures. J. Solid State Chem. 2019, 270, 346–359. [CrossRef]

5. Fisher, I.R.; Bud’ko, S.L.; Song, C.; Canfield, P.C.; Ozawa, T.C.; Kauzlarich, S.M. Yb14ZnSb11: Charge Balance in Zintl Compounds as a Route to Intermediate Yb Valence. Phys. Rev. Lett. 2000, 85, 1120–1123. [CrossRef] [PubMed] 6. Kauzlarich, S.M.; Brown, S.R.; Snyder, G.J. Zintl phases for thermoelectric devices. Dalton Trans. 2007, 21, 2099–2107. [CrossRef]

7. Mandrus, D.; Sefat, A.S.; McGuire, M.A.; Sales, B.C. Materials Chemistry of BaFe2As2: A Model Platform for Unconventional Superconductivity. Chem. Mater. 2010, 22, 715–723. [CrossRef] 8. Sales, B.C.; Mandrus, D.; Williams, R.K. Filled Skutterudite Antimonides: A New Class of . Science 1996, 272, 1325–1328. [CrossRef] Crystals 2020, 10, 475 11 of 13

9. Hu, Y.; Cerretti, G.; Wille, E.L.K.; Bux, S.K.; Kauzlarich, S.M. The remarkable crystal chemistry of the

Ca14AlSb11 structure type, magnetic and thermoelectric properties. J. Solid State Chem. 2019, 271, 88–102. [CrossRef] 10. Owens-Baird, B.; Wang, J.; Wang, S.G.; Chen, Y.S.; Lee, S.; Donadio, D.; Kovnir, K. III–V Clathrate

Semiconductors with Outstanding Hole Mobility: Cs8In27Sb19 and A8Ga27Sb19 (A = Cs, Rb). J. Am. Chem. Soc. 2020, 142, 2031–2041. [CrossRef] 11. Xia, S.Q.; Bobev, S. Cation-Anion Interactions as Structure Directing Factors: Structure and Bonding of

Ca2CdSb2 and Yb2CdSb2. J. Am. Chem. Soc. 2007, 129, 4049–4057. [CrossRef] 12. Xia, S.Q.; Bobev, S. Interplay between size and electronic effects in determining the homogeneity range of the A Zn Pn and A Cd Pn phases (0 x 0.5), A = Ca, Sr, Yb, Eu; Pn = Sb, Bi. J. Am. Chem. Soc. 2007, 9 4+x 9 9 4+x 9 ≤ ≤ 129, 10011–10018. [CrossRef][PubMed]

13. Xia, S.Q.; Bobev, S. Zintl phase variations through cation selection. Synthesis and structure of A21Cd4Pn18 (A = Eu, Sr, Ba; Pn = Sb, Bi). Inorg. Chem. 2008, 47, 1919–1921. [CrossRef][PubMed] 14. Saparov, B.; He, H.; Zhang, X.H.; Greene, R.; Bobev, S. Synthesis, crystallographic and theoretical studies of the

new Zintl phases Ba2Cd2Pn3 (Pn = As, Sb), and the solid solutions (Ba1–xSrx)2Cd2Sb3 and Ba2Cd2(Sb1–xAsx)3. Dalton Trans. 2010, 39, 1063–1070. [CrossRef][PubMed] 1 4– 15. Saparov, B.; Bobev, S. Isolated [ZnPn2] Chains in the Zintl Phases Ba2ZnPn2 (Pn = As, Sb, Bi) - Synthesis, ∞ Structure, and Bonding. Inorg. Chem. 2010, 49, 5173–5179. [CrossRef][PubMed]

16. Wilson, D.K.; Saparov, B.; Bobev, S. Synthesis, Crystal Structures and Properties of the Zintl Phases Sr2ZnP2, Sr2ZnAs2, A2ZnSb2 and A2ZnBi2 (A = Sr and Eu). Z. Anorg. Allg. Chem. 2011, 637, 2018–2025. [CrossRef] 17. He, H.; Tyson, C.; Saito, M.; Bobev, S. Synthesis and structural characterization of the ternary Zintl phases

AE3Al2Pn4 and AE3Ga2Pn4 (AE = Ca, Sr, Ba, Eu; Pn = P, As). J. Solid State Chem. 2012, 188, 59–65. [CrossRef] 18. Zimmer, B.I.; Jeitschko, W.; Albering, J.H.; Glaum, R.; Reehuis, M. The rare earth oxides LnFePO, LnRuPO and LnCoPO with ZrCuSiAs type structure. J. Alloys Compd. 1995, 229, 238–242. [CrossRef] 19. Kamihara, Y.; Hiramatsu, H.; Hirano, M.; Kawamura, R.; Yanagi, H.; Kamiya, T.; Hosono, H. -Based Layered Superconductor: LaOFeP. J. Am. Chem. Soc. 2006, 128, 10012–10013. [CrossRef] 20. Ren, Z.A.; Che, G.C.; Dong, X.L.; Yang, J.; Lu, W.; Yi, W.; Shen, X.L.; Li, Z.C.; Sun, L.L.; Zhou, F.; et al.

Superconductivity and phase diagram in iron-based arsenic-oxides ReFeAsO1–δ (Re = rare-earth metal) without fluorine doping. EPL 2008, 83, 17002. [CrossRef] 21. Wang, X.C.; Yu, J.; Ruan, B.B.; Pan, B.J.; Mu, Q.G.; Liu, T.; Zhao, K.; Chen, G.F.; Ren, Z.A. Revisiting the Electron-Doped SmFeAsO: Enhanced Superconductivity up to 58.6 K by Th and F Codoping. Chinese Phys. Lett. 2017, 34, 077401. [CrossRef]

22. Xia, S.Q.; Bobev, S. On the existence of Ca2Bi-crystal and electronic structure of Ca4Bi2O. J. Alloys Compd. 2007, 427, 67–72. [CrossRef]

23. Xia, S.Q.; Bobev, S. Dibarium tricadmium bimuthide (-I,-III) oxide, Ba2Cd3-δBi3O. Acta Crystallogr. E. 2010, 66, i81. [CrossRef][PubMed]

24. Saparov, B.; Bobev, S. Synthesis, crystal and electronic structures of the new quaternary phases A5Cd2Sb5F (A = Sr, Ba, Eu), and Ba5Cd2Sb5Ox (0.5 < x < 0.7). Dalton Trans. 2010, 39, 11335–11343. [PubMed] 25. Saparov, B.; Bobev, S. Pentaeuropium dicadmium pentaantimonide oxide, Eu5Cd2Sb5O. Acta Crystallogr. E. 2011, E67, i11. [CrossRef][PubMed]

26. Darone, G.M.; Bobev, S. Ba5Cd2Sb4O2 —A New Antimonide Oxide with a Complex Structure. Crystals 2011, 1, 206–214. [CrossRef]

27. Wang, Y.; Darone, G.M.; Bobev, S. The New Zintl Phases Eu21Cd4Sb18 and Eu21Mn4Sb18. J. Solid State Chem. 2016, 238, 303–310. [CrossRef] 28. Wang, J.; Yang, M.; Pan, M.Y.; Xia, S.Q.; Tao, X.T.; He, H.; Darone, G.; Bobev, S. Synthesis, Crystal and

Electronic Structures, and Properties of the New Pnictide Semiconductors A2CdPn2 (A = Ca, Sr, Ba, Eu; Pn = P, As). Inorg. Chem. 2011, 50, 8020–8027. [CrossRef] 29. Makongo, J.P.A.; Darone, G.M.; Xia, S.Q.; Bobev, S. Non-stoichiometric Compositions arising from synergistic

electronic and size effects. Synthesis, Crystal Chemistry and Electronic Properties of the A14Cd1+xPn11 Compounds (0 x 0.3; A = Sr, Eu; Pn = As, Sb). J. Mater. Chem. 2015, 3, 10388–10400. ≤ ≤ 30. Saparov, B.; Bobev, S. Undecaeuropium hexazinc dodecaarsenide. Acta Crystallogr. E. 2010, 66, i24. [CrossRef] Crystals 2020, 10, 475 12 of 13

31. Baranets, S.; He, H.; Bobev, S. -bearing arsenides and germanides from elemental mixtures not involving niobium: A new twist to an old problem in solid-state synthesis. Acta Crystallogr. C. 2018, 74, 623–627. [CrossRef] 32. SAINT; Bruker AXS Inc.: Madison, WI, USA, 2014. 33. SADABS; Bruker AXS Inc.: Madison, WI, USA, 2014. 34. Sheldrick, G.M. SHELXT – Integrated space-group and crystal-structure determination. Acta Crystallogr. A. 2015, 71, 3–8. [CrossRef][PubMed] 35. Sheldrick, G.M. Crystal structure refinement with SHELXL. Acta Crystallogr. C. 2015, 71, 3–8. [CrossRef] [PubMed] 36. Gelato, L.M.; Parthé, E. STRUCTURE TIDY. J. Appl. Crystallogr. 1987, 20, 139–143. [CrossRef] 37. Jespen, O.; Andersen, O.K. The Stuttgart TB-LMTO-ASA Program; MPI für Festkörperforschung: Stuttgart, Germany, 1998. 38. Von Barth, U.; Hedin, L. A local exchange-correlation potential for the spin polarized case: I. J. Phys. C Solid State Phys. 1972, 5, 1629–1642. [CrossRef] 39. Dronskowski, R.; Bloechl, P.E. Crystal orbital Hamilton populations (COHP): Energy-resolved visualization of chemical bonding in solids based on density-functional calculations. J. Phys. Chem. 1993, 97, 9617–9624. [CrossRef]

40. He, H.; Stoyko, S.S.; Mar, A.; Bobev, S. Ternary K2Zn5As4-type pictides Rb2Cd5As4 and Rb2Zn5Sb4, and the solid solution Rb2Cd5(As,Sb)4. Acta. Crystallogr. C. 2013, 69, 455–459. [CrossRef] 41. Pauling, L. Atomic Radii and Interatomic Distances in Metals. J. Am. Chem. Soc. 1947, 69, 542–553. [CrossRef] 3– 42. He, H.; Tyson, C.; Bobev, S. New Compounds with [As7] Clusters: Synthesis and Crystal Structures of the Zintl Phases Cs2NaAs7, Cs4ZnAs14 and Cs4CdAs14. Crystals 2011, 1, 87–98. [CrossRef] 43. Suen, N.-T.; Wang, Y.; Bobev, S. Synthesis, Crystal Structures, and Physical Properties of the New Zintl Phases

A21Zn4Pn18 (A = Ca, Eu; Pn = As, Sb)—Versatile Arrangements of [ZnPn4] Tetrahedra. J. Solid State Chem. 2015, 227, 204–211. [CrossRef]

44. Stoyko, S.S.; Khatun, M.; Mar, A. Ternary Arsenides A2Zn2As3 (A = Sr, Eu) and Their Stuffed Derivatives A2Ag2ZnAs3. Inorg. Chem. 2012, 51, 2621–2628. [CrossRef] 45. Childs, A.B.; Baranets, S.; Bobev, S. Five new ternary -arsenides discovered. Synthesis and structural

characterization of the Zintl phases Sr3In2As4, Ba3In2As4, Eu3In2As4, Sr5In2As6 and Eu5In2As6. J. Solid State Chem. 2019, 278, 120889. [CrossRef] 46. Baranets, S.; Darone, G.M.; Bobev, S. Synthesis and structure of Sr Zn As and Eu Zn As (x 14 1+x 11 14 1+x 11 ≤ 0.5). New members of the family of pnictides isotypic with Ca14AlSb11, exhibiting a new type of structural disorder. J. Solid State Chem. 2019, 280, 120990. [CrossRef]

47. Stoyko, S.S.; Khatun, M.; Mar, A. Ternary Arsenides A2Zn5As4 (A = K, Rb): Zintl Phases Built from Stellae Quandrangulae. Inorg. Chem. 2012, 51, 9517–9521. [CrossRef][PubMed] 48. Saparov, B.; Broda, M.; Ramanujachary, K.V.; Bobev, S. New quaternary Zintl phases - Synthesis, crystal and

electronic structures of KA2Cd2Sb3 (A = Ca, Sr, Ba, Eu, Yb). Polyhedron 2010, 29, 456–462. [CrossRef] 49. Wang, Y.; Calvert, L.D.; Gabe, E.J.; Taylor, J.B. Europium Arsenic Oxide Eu4As2O: A Filled La2Sb Structure and its Relation to the K2NiF4 and GeTeU Types. Acta Crystallogr. B. 1977, 33, 3122–3125. [CrossRef] 50. Wang, Y.; Calvert, L.D.; Smart, M.L.; Taylor, J.B. Structure of Trieuropium Triarsenide- Oxide (1:1). Acta Crystallogr. B. 1980, 36, 131–133. [CrossRef]

51. Sanders, M.B.; Krizan, J.W.; Cava, R.J. RE3Sb3Zn2O14 (RE = La, Pr, Nd, Sm, Eu, Gd): A new family of pyrochlore derivatives with rare earth ions on a 2D Kagome lattice. J. Mater. Chem. C. 2016, 4, 541–550. [CrossRef] 52. Baranets, S.; Bobev, S. From the Ternary Phase Ca Zn Sb (δ 0.4) to the Quaternary Solid Solutions 14 1+δ 11 ≈ Ca RExZnSb (RE = La–Nd, Sm, Gd, x 0.9). A Tale of Electron Doping via Rare-Earth Metal Substitutions 14–x 11 ≈ and the Concomitant Structural Transformations. Inorg. Chem. 2019, 58, 8506–8516. [CrossRef]

53. Hu, Y.; Wang, J.; Kawamura, A.; Kovnir, K.; Kauzlarich, S.M. Yb14MgSb11 and Ca14MgSb11 – New Mg-Containing Zintl Compounds and Their Structures, Bonding, and Thermoelectric Properties. Chem. Mater. 2015, 27, 343–351. [CrossRef] 54. Baranets, S.; Voss, L.; Stoyko, S.; Bobev, S. Synthesis, crystal structure and physical properties of the solid solutions Ca RExCdSb (RE = La–Nd, Sm, Gd–Yb, x 0.85 0.15). J. Appl. Phys. 2019, 125, 245101. 14–x 11 ≈ ± [CrossRef] Crystals 2020, 10, 475 13 of 13

55. Prakash, J.; Stoyko, S.; Voss, L.; Bobev, S. On the Extended Series of Quaternary Zintl Phases Ca13REMnSb11 (RE = La–Nd, Sm, Gd–Dy). Eur. J. Inorg. Chem. 2016, 18, 2912–2922. [CrossRef] 56. Ovchinnikov, A.; Prakash, J.; Bobev, S. Crystal chemistry and magnetic properties of the solid solutions Ca RExMnBi (RE = La–Nd, Sm, and Gd–Ho; x 0.6–0.8). Dalton Trans. 2017, 46, 16041–16049. [CrossRef] 14–x 11 ≈ [PubMed]

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